JP5218065B2 - Austenitic stainless steel welded joints and austenitic stainless steel welded materials - Google Patents

Austenitic stainless steel welded joints and austenitic stainless steel welded materials Download PDF

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JP5218065B2
JP5218065B2 JP2008553981A JP2008553981A JP5218065B2 JP 5218065 B2 JP5218065 B2 JP 5218065B2 JP 2008553981 A JP2008553981 A JP 2008553981A JP 2008553981 A JP2008553981 A JP 2008553981A JP 5218065 B2 JP5218065 B2 JP 5218065B2
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stainless steel
austenitic stainless
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JPWO2008087807A1 (en
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孝裕 小薄
和博 小川
浩一 岡田
正晃 五十嵐
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3053—Fe as the principal constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12944—Ni-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12958—Next to Fe-base component
    • Y10T428/12965—Both containing 0.01-1.7% carbon [i.e., steel]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
    • Y10T428/12979—Containing more than 10% nonferrous elements [e.g., high alloy, stainless]

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Arc Welding In General (AREA)
  • Heat Treatment Of Steel (AREA)

Description

本発明は、オーステナイト系ステンレス鋼溶接継手およびオーステナイト系ステンレス鋼溶接材料に関する。詳しくは、鋼管、鋼板等として、高温強度と耐食性が求められる用途に幅広く適用できることはもちろん、０．０４％を超える高い量のＰを含むにも拘わらず優れた耐溶接凝固割れ性も有するオーステナイト系ステンレス鋼溶接継手およびオーステナイト系ステンレス鋼溶接材料に関する。   The present invention relates to an austenitic stainless steel welded joint and an austenitic stainless steel welded material. Specifically, austenite having excellent weld solidification cracking resistance in spite of containing a high amount of P exceeding 0.04%, as well as being widely applicable to applications requiring high temperature strength and corrosion resistance, such as steel pipes and steel plates. The present invention relates to a stainless steel welded joint and an austenitic stainless steel weld material.

オーステナイト系ステンレス鋼は、例えば、ＪＩＳ Ｇ ４３０４（２００５）に規定されたＳＵＳ３０４やＳＵＳ３１６、ＳＵＳ３１０Ｓ等のように、ＣｒおよびＮｉを主要元素とした耐食性に優れた材料である。   Austenitic stainless steel is a material having excellent corrosion resistance with Cr and Ni as main elements, such as SUS304, SUS316, and SUS310S defined in JIS G 4304 (2005), for example.

しかしながら、いずれのオーステナイト系ステンレス鋼にも構成元素の含有量には制限が設けられており、特に不純物元素であるＰは一般に０．０４５％以下に規制されているのが現状である。さらに、その溶接に用いる溶接材料として、例えばＪＩＳ Ｇ ４３１６（１９９１）では、オーステナイト系の溶接用ステンレス鋼線材のＰはさらに低い０．０３０％以下に規制されている。   However, any austenitic stainless steel is limited in the content of constituent elements, and in particular, the impurity element P is generally regulated to 0.045% or less. Further, as a welding material used for the welding, for example, in JIS G 4316 (1991), P of the austenitic stainless steel wire for welding is regulated to 0.030% or less, which is even lower.

一方、本来不純物元素であるＰを高濃度で含有させると、Ｍ２３Ｃ６炭化物の微細化による析出硬化に寄与し、クリープ強度が向上することが知られている。On the other hand, it is known that when P, which is originally an impurity element, is contained at a high concentration, it contributes to precipitation hardening due to the refinement of M 23 C 6 carbide and improves the creep strength.

このため、例えば、特許文献１〜３に、高い濃度でＰを含有させた技術が提案されている。   For this reason, for example, Patent Documents 1 to 3 propose a technique in which P is contained at a high concentration.

すなわち、特許文献１に、Ｐを０．０５〜０．４０％含有させて、Ｐの析出硬化促進作用によって著しく高温強度を高めた「弁用耐熱鋼の改良」が開示されている。   That is, Patent Document 1 discloses “improving heat resistant steel for valves” in which P is contained in an amount of 0.05 to 0.40% and the high temperature strength is remarkably increased by the precipitation hardening promoting effect of P.

また、特許文献２に、Ｃの含有量を０．０１％以下とした極低炭素のオーステナイトステンレス鋼に０．０３〜０．０８％のＰを含有させた「クリープ強度に優れたオーステナイトステンレス鋼」が開示されている。   Further, Patent Document 2 discloses that an austenitic stainless steel excellent in creep strength is obtained by adding 0.03 to 0.08% of P to an extremely low carbon austenitic stainless steel having a C content of 0.01% or less. Is disclosed.

さらに、特許文献３に、Ｐを０．０５〜０．３０％含有させた高温強度に優れた「オーステナイト系ステンレス鋼」が開示されている。   Furthermore, Patent Document 3 discloses “austenite stainless steel” containing 0.05 to 0.30% of P and excellent in high temperature strength.

このように、Ｐを高濃度で含有させると、Ｍ２３Ｃ６炭化物の微細化に寄与しクリープ強度を高めることができる。Thus, when P is contained in a high concentration, it contributes to refinement of M 23 C 6 carbide and can increase the creep strength.

しかしながら、特に、ＳＵＳ３１０Ｓのような完全オーステナイト凝固するオーステナイト系ステンレス鋼におけるＰ含有量の増加は、溶接性の低下を招いてしまう。すなわち、特に溶接凝固過程の終了期に近い、主として結晶粒界に膜状の液相が存在する段階において、凝固収縮または熱収縮により加わる歪みが溶接金属の変形能以上になった場合に生じる割れ（以下、「溶接凝固割れ」という。）の発生を著しく増加させてしまう。   However, an increase in the P content particularly in an austenitic stainless steel that completely solidifies austenite, such as SUS310S, causes a decrease in weldability. That is, cracks that occur when the strain applied by solidification shrinkage or thermal shrinkage exceeds the deformability of the weld metal, especially in the stage where a film-like liquid phase exists mainly near the end of the welding solidification process. (Hereinafter referred to as “weld solidification cracking”) is significantly increased.

このため、多量のＰ含有は、特に、完全オーステナイト凝固するオーステナイト系ステンレス鋼の場合には、溶接性という観点からの制限を受けることになり、例えば、非特許文献１において、Ｐの含有量は厳しく制限すべきであることが示されている。   For this reason, a large amount of P content is restricted from the viewpoint of weldability, particularly in the case of austenitic stainless steel that is completely austenitic solidified. For example, in Non-Patent Document 1, the content of P is It is shown that it should be strictly limited.

特許文献１で開示された技術は、排気弁やストップバルブ弁等の用途には好適であるものの、Ｐを多量に含有させることによる溶接凝固割れ感受性の著しい増大に関しては何の配慮もなされていない。したがって、溶接を必要とするような鋼材としての使用は極めて困難であり、特に、完全オーステナイト凝固するようなオーステナイト系ステンレス鋼材として用いることはできないものであった。   Although the technique disclosed in Patent Document 1 is suitable for applications such as an exhaust valve and a stop valve valve, no consideration is given to a marked increase in weld solidification cracking susceptibility by containing a large amount of P. . Therefore, it is extremely difficult to use as a steel material that requires welding, and in particular, it cannot be used as an austenitic stainless steel material that solidifies completely austenite.

また、特許文献２には、溶接性を損なわないためにＰの含有量の上限を０．０８％にすることが記載されているだけであって、初晶オーステナイト凝固特に完全オーステナイト凝固するようなオーステナイト系ステンレス鋼の溶接凝固割れ感受性の低減について配慮すべきことは全く記載されていない。したがって、特許文献２で開示されたオーステナイトステンレス鋼を、特に、完全オーステナイト凝固するようなオーステナイト系ステンレス鋼材として用いることはできなかった。   Patent Document 2 only describes that the upper limit of the P content is 0.08% so as not to impair the weldability, and primary austenite solidification, particularly complete austenite solidification. There is no mention at all of what should be considered about the reduction of weld solidification cracking susceptibility of austenitic stainless steel. Therefore, the austenitic stainless steel disclosed in Patent Document 2 could not be used particularly as an austenitic stainless steel material that completely solidifies austenite.

特許文献３で開示された技術は、確かに、鋼管、鋼板、棒鋼、鋳鋼品、鍛鋼品等として、高温強度と耐食性が求められる用途に幅広く適用することができるものである。しかしながら、完全オーステナイト凝固するようなオーステナイト系ステンレス鋼における高Ｐ化に伴う溶接凝固割れについての検討は十分にはなされていない。したがって、特許文献３で開示されたオーステナイト系ステンレス鋼を、完全オーステナイト凝固するオーステナイト系ステンレス鋼材として用いた場合、必ずしも優れた耐溶接凝固割れ性が確保できるというものではなかった。   The technique disclosed in Patent Document 3 can be widely applied to applications that require high-temperature strength and corrosion resistance, such as steel pipes, steel plates, steel bars, cast steel products, and forged steel products. However, the examination of weld solidification cracking accompanying the increase in P in austenitic stainless steel that solidifies completely austenite has not been made sufficiently. Therefore, when the austenitic stainless steel disclosed in Patent Document 3 is used as an austenitic stainless steel material that solidifies completely austenite, it is not always possible to ensure excellent weld solidification cracking resistance.

特公昭３７−１７１１３号公報Japanese Examined Patent Publication No. 37-17113 特開昭６２−２６７４５４号公報Japanese Patent Laid-Open No. 62-267454 ＷＯ２００６／１０６９４４号公報WO 2006/106944 Ｙ．Ａｒａｔａ、Ｆ．Ｍａｔｓｕｄａ ａｎｄ Ｓ．Ｋａｔａｙａｍａ：Ｔｒａｎｓａｃｔｉｏｎｓ ｏｆ ＪＷＲＩ、Ｖｏｌ．６−１（１９７７）ｐｐ１０５−１１６Y. Arata, F.A. Matsuda and S.M. Katayama: Transactions of JWRI, Vol. 6-1 (1977) pp105-116

本発明の目的は、Ｐ含有量が高く、しかも、完全オーステナイト凝固するにも拘わらず、溶接性、なかでも耐溶接凝固割れ性に優れたオーステナイト系ステンレス鋼溶接継手とオーステナイト系ステンレス鋼溶接材料を提供することにある。   An object of the present invention is to provide an austenitic stainless steel welded joint and an austenitic stainless steel welding material that have a high P content and are excellent in weldability, in particular, weld solidification crack resistance despite complete austenite solidification. It is to provide.

本発明者らは、従来クリープ強度の向上等鉄鋼材料の特性に良い影響を及ぼすことが知られているにも拘わらず、溶接凝固割れ感受性を著しく増大させるためにその含有量が抑制されていたＰを高い濃度で含み、かつ完全オーステナイト凝固するオーステナイト系ステンレス鋼について、溶接凝固割れを防止して良好な溶接性を具備させることを目的に種々の検討を実施した。   In spite of the fact that the present inventors have been known to have a good effect on the properties of steel materials such as the improvement of creep strength, the content has been suppressed in order to significantly increase the weld solidification cracking susceptibility. Various studies were conducted on austenitic stainless steel containing P at a high concentration and completely solidified with austenite for the purpose of preventing weld solidification cracking and providing good weldability.

なお、溶接凝固割れは、前述のように、溶接凝固中のデンドライト間に残存する液相が低温域まで膜状に残存する場合に、付加される応力に耐えられずに生じる割れである。   As described above, the weld solidification crack is a crack that occurs without being able to withstand the applied stress when the liquid phase remaining between the dendrites during the weld solidification remains in the form of a film up to a low temperature range.

そして、Ｐ含有量の増加によって溶接凝固割れ感受性が増大する、つまり、溶接凝固割れの発生が多くなるのは、Ｐが凝固中の液相に著しく濃化して液相の凝固完了温度を大きく低下させるため、液相がより低温域まで残存することに起因するものである。   The increase in the P content increases the weld solidification cracking susceptibility. In other words, the occurrence of weld solidification cracking increases because the P is significantly concentrated in the liquid phase during solidification and the solidification temperature of the liquid phase is greatly reduced. Therefore, the liquid phase is caused to remain up to a lower temperature range.

このため、不純物元素として含まれるＰに起因する溶接凝固割れの発生低減のための研究が種々行われているものの、Ｐはオーステナイト中にはほとんど固溶しないため、初晶オーステナイト凝固する場合はもちろんのこと、完全オーステナイトにて凝固する場合に至っては溶接凝固割れ感受性を著しく増大させてしまう。   For this reason, although various studies for reducing the occurrence of weld solidification cracking due to P contained as an impurity element have been conducted, P is hardly dissolved in austenite, so of course when primary austenite solidifies. That is, when solidified with complete austenite, the weld solidification cracking sensitivity is remarkably increased.

このため、特に完全オーステナイト凝固するステンレス鋼ではＰ含有量に対する規制が設けられており、例えば、上記完全オーステナイト凝固するオーステナイト系ステンレス鋼の代表鋼種であるＪＩＳ Ｇ ４３０４（２００５）に規定されたＳＵＳ３１０Ｓでは、Ｐの含有量は０．０４５％以下に制限され、その溶接に用いられる溶接材料は溶接凝固割れを配慮し、ＪＩＳ Ｇ ４３１６（１９９１）ではさらに低い０．０３０％以下に制限されているのが実状である。   For this reason, there is a restriction on the P content particularly in fully austenitic solidified stainless steel. For example, in SUS310S defined in JIS G 4304 (2005), which is a representative steel type of austenitic stainless steel that is completely austenitic solidified. The content of P is limited to 0.045% or less, and the welding material used for welding is limited to 0.030% or less, which is lower in JIS G 4316 (1991) in consideration of weld solidification cracking. Is real.

しかしながら、前述のとおり、Ｐはクリープ強度等を向上させる元素として知られているため、完全オーステナイト凝固するステンレス鋼に対して凝固割れ感受性の低減が可能となった場合、例えば高温環境下で使用されるボイラや化学プラントの素材として使用されるオーステナイト系ステンレス鋼の著しい高機能化、すなわち優れた高温強度および組織安定性等の確保に大いに寄与することができると考えられる。   However, as described above, since P is known as an element that improves the creep strength and the like, when it becomes possible to reduce the solidification cracking susceptibility to a fully austenitic solidified stainless steel, it is used in a high temperature environment, for example. It is thought that it can greatly contribute to the remarkable enhancement of functionality of austenitic stainless steel used as a raw material for boilers and chemical plants, that is, to ensure excellent high-temperature strength and structural stability.

そこで、本発明者らは、Ｐを高い濃度で含み、完全オーステナイト凝固するオーステナイト系ステンレス鋼の溶接凝固割れ感受性の低減の可能性について調査を行った。   Therefore, the present inventors investigated the possibility of reducing the weld solidification cracking susceptibility of austenitic stainless steel that contains P at a high concentration and solidifies completely austenite.

先ず、本発明者らは、溶接凝固中にオーステナイトに固溶しないために液相中へ著しく濃化したＰを燐化物として固定し、これを液相中から晶出させれば、たとえ最も凝固割れ感受性の高い完全オーステナイト凝固する場合であっても、凝固割れ感受性に大きな影響を及ぼす液相を早期に消失させることができると考え、Ｐとの親和力が大きくＰを固定化する能力の高い元素について検討した。   First, the present inventors fixed P, which was remarkably concentrated in the liquid phase as a phosphide because it was not dissolved in austenite during weld solidification, and crystallized it from the liquid phase, even if it solidifies most. Even when complete austenite solidification with high cracking susceptibility is considered, the liquid phase that greatly affects the susceptibility to solidification cracking can be eliminated early, and the element has a high affinity for P and a high ability to immobilize P. Was examined.

その結果、希土類元素（以下、「ＲＥＭ」ともいう。）がＰとの親和力が大きい元素であること、すなわち、Ｐ固定化能が非常に高い元素であるとの知見が得られた。   As a result, it was found that the rare earth element (hereinafter also referred to as “REM”) is an element having a large affinity for P, that is, an element having a very high P immobilization ability.

なお、「ＲＥＭ」とは、Ｓｃ、Ｙおよびランタノイドの合計１７元素の総称である。   “REM” is a generic name for a total of 17 elements of Sc, Y and lanthanoids.

そこで本発明者らは、次に、燐化物の晶出を考慮したミクロ偏析計算モデルを作成して、Ｐの凝固割れ感受性に対する悪影響を無害化するために必要なＲＥＭの含有量を予測した。   Therefore, the present inventors next created a microsegregation calculation model in consideration of the crystallization of phosphide, and predicted the REM content necessary for detoxifying the adverse effect on the solidification cracking sensitivity of P.

その結果、ＲＥＭの含有量が０．２％を超えて０．６％以下の範囲であれば、液相の早期晶出が促進され、凝固割れ感受性を低減することが可能となる場合のあることが判明した。   As a result, if the content of REM is in the range of more than 0.2% and not more than 0.6%, early crystallization of the liquid phase may be promoted, and it may be possible to reduce solidification cracking susceptibility. It has been found.

なお、上記ＲＥＭの含有量とは、ＲＥＭの中の１種または２種以上の元素の合計含有量を指す。   The REM content refers to the total content of one or more elements in the REM.

そこでさらに、本発明者らは、実際にＰを質量％で、０．１％含有する種々の完全オーステナイト凝固するオーステナイト系ステンレス鋼を作製し、ＲＥＭの含有量を変化させた場合の溶接凝固割れ感受性について詳細な調査を行った。   Therefore, the present inventors further produced various solid austenitic austenitic stainless steels containing 0.1% P by mass% and weld solidification cracks when the content of REM was changed. A detailed investigation was conducted on sensitivity.

その結果、Ｐの影響を含めた下記の（１）式または（２）式を満足させることによって完全オーステナイト凝固するように成分設計された高Ｐのオーステナイト系ステンレス鋼の場合には、数値計算により予測された「０．２％を超えて０．６％以下」という適正量のＲＥＭを含有しておれば、完全オーステナイト凝固下で、０．１％という高い量のＰを含有する場合でも溶接凝固割れの発生を抑制できることが判明した。   As a result, in the case of a high P austenitic stainless steel that is designed to completely solidify austenite by satisfying the following formula (1) or (2) including the influence of P, numerical calculation is performed. If the predicted amount of REM is more than 0.2% and not more than 0.6%, welding is possible even when containing a high amount of 0.1% P under complete austenite solidification. It has been found that the occurrence of solidification cracks can be suppressed.

（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）＜１．３８８・・・（１）、
（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）＜１．３８８・・・（２）。
ここで（１）式および（２）式中の元素記号は、その元素の質量％での含有量を表す。(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P) <1.388 (1),
(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P) <1.388 (2).
Here, the element symbols in the formulas (1) and (2) represent the content in mass% of the element.

本発明は、上記の知見に基づいて完成されたものであり、その要旨は、下記（１）および（２）に示すオーステナイト系ステンレス鋼溶接継手、ならびに（３）および（４）に示すオーステナイト系ステンレス鋼溶接材料にある。   The present invention has been completed based on the above findings, and the gist thereof is the austenitic stainless steel welded joint shown in the following (1) and (2), and the austenitic system shown in (3) and (4). In stainless steel welding material.

（１）母材および溶接金属が、質量％で、Ｃ：０．３％以下、Ｓｉ：１％以下、Ｍｎ：０．０１〜３．０％、Ｐ：０．０４％を超えて０．３％以下、Ｓ：０．０１％以下、Ｃｒ：１２〜３０％、Ｎｉ：１０〜４０％、希土類元素：０．２％を超えて０．６％以下、ｓｏｌ．Ａｌ：０．００１〜３％およびＮ：０．３％以下を含有し、残部がＦｅおよび不純物からなり、かつ下記（１）式を満足することを特徴とするオーステナイト系ステンレス鋼溶接継手。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）＜１．３８８・・・（１）。
ここで（１）式中の元素記号は、その元素の質量％での含有量を表す。
(1) Base material and weld metal in mass%, C: 0.3% or less, Si: 1% or less, Mn: 0.01 to 3.0%, P: more than 0.04% and 0.0. 3% or less, S: 0.01% or less, Cr: 12-30%, Ni: 10-40% , rare earth elements: more than 0.2% and 0.6% or less, sol. An austenitic stainless steel welded joint containing Al: 0.001 to 3% and N: 0.3% or less, the balance being Fe and impurities, and satisfying the following formula (1).
(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P) <1.388 (1).
Here, the element symbol in the formula (1) represents the content in mass% of the element.

（２）Ｆｅの一部に代えて、質量％で、さらに、下記第１群および第２群の中から選ばれた１種または２種以上の元素を含有し、かつ下記（２）式を満足することを特徴とする請求項１に記載のオーステナイト系ステンレス鋼溶接継手。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）＜１．３８８・・・（２）。
ここで（２）式中の元素記号は、その元素の質量％での含有量を表す。
第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上、
第２群：Ｃａ：０．０５％以下およびＭｇ：０．０５％以下の１種または２種。
(2) Instead of a part of Fe, in mass%, further containing one or more elements selected from the following first group and second group, and the following formula (2): 2. The austenitic stainless steel welded joint according to claim 1, wherein the welded joint is satisfactory.
(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P) <1.388 (2).
Here, the element symbol in the formula (2) represents the content in mass% of the element.
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: 1.5% or less , B: 0.03% or less, Cu: 3% or less and Co: 5% or less
Second group: one or two of Ca: 0.05% or less and Mg: 0.05% or less.

（３）質量％で、Ｃ：０．３％以下、Ｓｉ：１％以下、Ｍｎ：０．０１〜３．０％、Ｐ：０．０４％超えて０．３％以下、Ｓ：０．０１％以下、Ｃｒ：１２〜３０％、Ｎｉ：１０〜４０％、希土類元素：０．２％超えて０．６％以下、ｓｏｌ．Ａｌ：０．００１〜３％およびＮ：０．３％以下を含有し、残部がＦｅおよび不純物からなり、かつ下記（１）式を満足することを特徴とするオーステナイト系ステンレス鋼溶接材料。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）＜１．３８８・・・（１）。
ここで（１）式中の元素記号は、その元素の質量％での含有量を表す。
(3) By mass%, C: 0.3% or less, Si: 1% or less, Mn: 0.01 to 3.0 %, P: more than 0.04% and 0.3% or less, S: 0.0. 01% or less, Cr: 12 to 30%, Ni: 10 to 40% , rare earth element: more than 0.2% to 0.6% or less, sol. An austenitic stainless steel welding material characterized by containing Al: 0.001 to 3% and N: 0.3% or less, the balance being Fe and impurities, and satisfying the following formula (1).
(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P) <1.388 (1).
Here, the element symbol in the formula (1) represents the content in mass% of the element.

（４）Ｆｅの一部に代えて、質量％で、さらに、下記第１群および第２群の中から選ばれた１種または２種以上の元素を含有し、かつ下記（２）式を満足することを特徴とする請求項３に記載のオーステナイト系ステンレス鋼溶接材料。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）＜１．３８８・・・（２）。
ここで（２）式中の元素記号は、その元素の質量％での含有量を表す。
第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上、
第２群：Ｃａ：０．０５％以下およびＭｇ：０．０５％以下の１種または２種。
(4) In place of part of Fe, in mass%, further containing one or more elements selected from the following first group and second group, and the following formula (2): The austenitic stainless steel welding material according to claim 3, wherein the welding material is satisfactory.
(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P) <1.388 (2).
Here, the element symbol in the formula (2) represents the content in mass% of the element.
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: 1.5% or less , B: 0.03% or less, Cu: 3% or less and Co: 5% or less
Second group: one or two of Ca: 0.05% or less and Mg: 0.05% or less.

以下、上記（１）および（２）に示すオーステナイト系ステンレス鋼溶接継手、ならびに（３）および（４）に示すオーステナイト系ステンレス鋼溶接材料に係る発明を、それぞれ、「本発明（１）」〜「本発明（４）」という。また、総称して「本発明」ということがある。   Hereinafter, the invention relating to the austenitic stainless steel welded joint shown in the above (1) and (2) and the austenitic stainless steel welded material shown in (3) and (4) are referred to as “present invention (1)” to This is referred to as “present invention (4)”. Also, it may be collectively referred to as “the present invention”.

本発明でいう「希土類元素（ＲＥＭ）」は、Ｓｃ、Ｙおよびランタノイドの合計１７元素の総称であり、ＲＥＭの含有量はＲＥＭの中の１種または２種以上の元素の合計含有量を指す。   The “rare earth element (REM)” as used in the present invention is a generic name for a total of 17 elements of Sc, Y and lanthanoid, and the content of REM refers to the total content of one or more elements in REM. .

本発明のオーステナイト系ステンレス鋼溶接継手は、Ｐ含有量が高く、しかも、完全オーステナイト凝固するにも拘わらず、溶接凝固割れの発生を抑制できるので、溶接施工が要求される用途に幅広く適用することができる。また、本発明のオーステナイト系ステンレス鋼溶接材料は、上記のオーステナイト系ステンレス鋼溶接継手を作製するのに最適である。   The austenitic stainless steel welded joint of the present invention has a high P content and can suppress the occurrence of weld solidification cracks despite complete austenite solidification, so that it can be widely applied to applications requiring welding construction. Can do. Moreover, the austenitic stainless steel welding material of the present invention is optimal for producing the austenitic stainless steel welded joint.

以下、本発明のオーステナイト系ステンレス鋼溶接継手および溶接材料における成分元素の限定理由について詳しく説明する。なお、以下の説明において、各元素の含有量の「％」表示は「質量％」を意味する。   Hereinafter, the reason for limitation of the component elements in the austenitic stainless steel welded joint and welding material of the present invention will be described in detail. In the following description, “%” display of the content of each element means “mass%”.

Ｃ：０．３％以下
Ｃは、オーステナイトを安定化させる元素であり、引張強度やクリープ強度を高める作用も有する。しかしながら、Ｃの含有量が過剰になり、特に、０．３％を超えると、溶接凝固割れ感受性が増大するとともに耐食性の著しい劣化をきたす。したがって、Ｃの含有量を０．３％以下とした。C: 0.3% or less C is an element that stabilizes austenite, and also has an effect of increasing tensile strength and creep strength. However, if the C content becomes excessive, especially exceeding 0.3%, the weld solidification cracking susceptibility increases and the corrosion resistance deteriorates significantly. Therefore, the content of C is set to 0.3% or less.

Ｃの上記したオーステナイトの安定化作用と引張強度やクリープ強度を高める作用を確保するためには、その含有量の下限は０．０５％とすることが好ましい。   In order to ensure the above-described C stabilizing effect of austenite and the effect of increasing tensile strength and creep strength, the lower limit of the content is preferably 0.05%.

なお、優れた耐食性が要求される場合、Ｃの含有量を低減することで耐粒界腐食性を高めることができ、高い温度領域でも使用可能となるので、高温領域で使用されかつ高い耐食性が要求される場合にはＣの含有量の上限は低減する方が好ましい。   When excellent corrosion resistance is required, the intergranular corrosion resistance can be increased by reducing the C content, and it can be used even in a high temperature range, so that it is used in a high temperature range and has high corrosion resistance. When required, it is preferable to reduce the upper limit of the C content.

したがって、オーステナイトの安定化、引張強度やクリープ強度の確保、良好な耐食性の確保という観点からのＣの好ましい含有量は０．０６％を超えて０．２５％以下であり、さらに好ましい含有量は０．０７〜０．１５％である。   Therefore, the preferable content of C from the viewpoint of stabilizing austenite, ensuring tensile strength and creep strength, and ensuring good corrosion resistance is more than 0.06% and 0.25% or less, and more preferable content is 0.07 to 0.15%.

Ｓｉ：２％以下
Ｓｉは、オーステナイト系ステンレス鋼の溶製時に脱酸作用を有し、また耐酸化性および耐水蒸気酸化性等を高めるのに有効な元素である。前記の効果を得るためには、Ｓｉは０．１％以上含有させるのが望ましい。しかしながら、その含有量が過剰になり、特に、２％を超えると、溶接凝固割れ感受性を著しく増大させるし、Ｓｉがフェライトを安定化させる元素であるために安定して完全オーステナイト凝固させてオーステナイト単相組織にすることが困難となる。したがって、Ｓｉの含有量は２％以下とした。なお、Ｓｉの好ましい含有量は１％以下である。Si: 2% or less Si is an element that has a deoxidizing action when austenitic stainless steel is melted and is effective in enhancing oxidation resistance, steam oxidation resistance, and the like. In order to acquire the said effect, it is desirable to contain Si 0.1% or more. However, if its content becomes excessive, particularly exceeding 2%, the weld solidification cracking susceptibility is remarkably increased, and since Si is an element that stabilizes ferrite, it is stably austenite solidified and austenite single. It becomes difficult to form a phase structure. Therefore, the Si content is set to 2% or less. In addition, the preferable content of Si is 1% or less.

Ｍｎ：０．０１〜３％
Ｍｎは、オーステナイトを安定化させる元素であるとともに、オーステナイト系ステンレス鋼中に不純物として含まれるＳによる熱間加工脆性の抑制の他、溶製時の脱酸効果に有効な元素である。このような効果を得るためには、Ｍｎは０．０１％以上含有させる必要がある。しかしながら、その含有量が３％を超えると、σ相等の金属間化合物相の析出を助長し、高温環境下で使用した場合には、高温における組織安定性の劣化に起因した靱性や延性の低下を生じる。したがって、Ｍｎの含有量は０．０１〜３％とした。なお、Ｍｎの含有量は０．０５〜２％であればより好ましく、０．１〜１．５％であればさらに好ましい。Mn: 0.01 to 3%
Mn is an element that stabilizes austenite, and is an element that is effective for the deoxidation effect during melting in addition to suppressing hot work brittleness due to S contained as impurities in the austenitic stainless steel. In order to acquire such an effect, it is necessary to contain Mn 0.01% or more. However, if its content exceeds 3%, it promotes the precipitation of intermetallic compound phases such as σ phase, and when used in a high temperature environment, the toughness and ductility decrease due to the deterioration of the structural stability at high temperatures. Produce. Therefore, the Mn content is set to 0.01 to 3%. The Mn content is more preferably 0.05 to 2%, and even more preferably 0.1 to 1.5%.

Ｐ：０．０４％を超えて０．３％以下
Ｐは、溶接凝固割れ感受性を著しく増大させる元素として知られており、特に完全オーステナイト凝固する場合にはその影響はより顕著となる。このため、従来、Ｐの含有量には規制が設けられてきたが、０．０４％を超えてＰを含有させれば炭化物の微細析出に寄与し、例えば高温環境下にて使用する場合のクリープ強度を向上させる等、材料の特性を向上させる効果が得られる。P: more than 0.04% but not more than 0.3% P is known as an element that remarkably increases the susceptibility to weld solidification cracking, and its influence becomes more remarkable particularly when complete austenite solidification occurs. For this reason, the content of P has been regulated in the past, but if P is contained in excess of 0.04%, it contributes to fine precipitation of carbides, for example when used in a high temperature environment. The effect of improving the properties of the material such as improving the creep strength can be obtained.

なお、本発明においては、後述する量のＲＥＭを含有させることによって、完全オーステナイト凝固下における溶接凝固割れ感受性増大に及ぼすＰの悪影響を排除しているものの、Ｐの含有量があまりにも過剰になり、特に、０．３％を超えると、クリープ延性の低下等の悪影響を避けられない。   In the present invention, the inclusion of the amount of REM described later eliminates the adverse effect of P on the increase in weld solidification cracking susceptibility under complete austenite solidification, but the P content becomes excessive. In particular, if it exceeds 0.3%, adverse effects such as a decrease in creep ductility cannot be avoided.

したがって、Ｐの含有量を０．０４％を超えて０．３％以下とした。なお、Ｐの好ましい含有量は０．０５％を超えて０．２５％以下であり、さらに好ましい含有量は０．０８％を超えて０．２％以下である。   Therefore, the P content is more than 0.04% and 0.3% or less. In addition, the preferable content of P is more than 0.05% and not more than 0.25%, and the more preferable content is more than 0.08% and not more than 0.2%.

Ｓ：０．０３％以下
Ｓは、オーステナイト系ステンレス鋼を溶製する際に原料などから混入してくる不純物元素であり、その含有量が多くなると、耐食性の低下を招くとともに、熱間加工性と溶接性も劣化させ、特に、Ｓの含有量が０．０３％を超えると、耐食性の低下、熱間加工性と溶接性の劣化が著しくなる。したがって、Ｓの含有量は０．０３％以下とした。なお、Ｓの含有量は可能な限り低減することが望ましいので、０．０１％以下とすればさらに好ましく、０．００５％以下とすれば極めて好ましい。S: 0.03% or less S is an impurity element mixed from raw materials when austenitic stainless steel is melted. When the content is increased, corrosion resistance is lowered and hot workability is increased. If the S content exceeds 0.03%, the corrosion resistance decreases, and the hot workability and weldability deteriorate significantly. Therefore, the content of S is set to 0.03% or less. In addition, since it is desirable to reduce the S content as much as possible, it is more preferably 0.01% or less, and extremely preferably 0.005% or less.

Ｃｒ：１２〜３０％
Ｃｒは、オーステナイト系ステンレス鋼の表面に薄い酸化皮膜を形成することによって、耐酸化性、耐水蒸気酸化性、耐高温腐食性等を確保させるための必須の元素である。前記した効果を得るためには、Ｃｒの含有量は１２％以上とする必要がある。なお、Ｃｒの含有量が多いほど耐食性は向上するが、Ｃｒがフェライトを安定化させる元素であるために、その含有量が３０％を超えると、オーステナイト組織が不安定となってσ相等の金属間化合物やα−Ｃｒ相を生成しやすくなるので、靱性や高温強度の劣化が生じる。したがって、Ｃｒの含有量は１２〜３０％とした。なお、Ｃｒの好ましい含有量は１５〜２８％であり、さらに好ましい含有量は１８〜２６％である。Cr: 12-30%
Cr is an essential element for ensuring oxidation resistance, steam oxidation resistance, high temperature corrosion resistance, and the like by forming a thin oxide film on the surface of austenitic stainless steel. In order to obtain the effects described above, the Cr content needs to be 12% or more. The corrosion resistance improves as the Cr content increases. However, since Cr is an element that stabilizes ferrite, if the content exceeds 30%, the austenite structure becomes unstable and a metal such as a σ phase. Since intermetallic compounds and α-Cr phases are easily generated, toughness and high-temperature strength are deteriorated. Therefore, the Cr content is 12-30%. In addition, the preferable content of Cr is 15 to 28%, and the more preferable content is 18 to 26%.

Ｎｉ：６〜５５％
Ｎｉは、安定なオーステナイト組織を確保するために必須の元素であり、その必要最少含有量は、オーステナイト系ステンレス鋼中に含まれるＣｒ、Ｍｏ、Ｗ、Ｎｂ等のフェライト生成元素やＭｎ、Ｃ、Ｎ等のオーステナイト生成元素の含有量によって定まる。Ni: 6-55%
Ni is an essential element for securing a stable austenite structure, and the necessary minimum content thereof is ferrite-forming elements such as Cr, Mo, W, and Nb contained in the austenitic stainless steel, Mn, C, It is determined by the content of austenite-generating elements such as N.

本発明では１２％以上のＣｒを含有させる必要があり、このＣｒ量に対してＮｉの含有量が６％未満の場合には、完全オーステナイト凝固させてオーステナイト単相組織にすることが困難となる。一方、Ｎｉの含有量が５５％を超える場合、オーステナイトに固溶し難いＰの液相中への濃化が著しくなるため、溶接凝固割れ感受性の増大を招く。したがって、Ｎｉの含有量は６〜５５％とした。なお、Ｎｉの好ましい含有量は１０〜４０％であり、さらに好ましい含有量は１５％を超えて３０％以下である。   In the present invention, it is necessary to contain 12% or more of Cr. When the content of Ni is less than 6% with respect to the amount of Cr, it is difficult to solidify completely austenite to obtain an austenite single phase structure. . On the other hand, when the Ni content exceeds 55%, the concentration of P, which is difficult to dissolve in austenite, into the liquid phase becomes significant, leading to increased weld solidification cracking susceptibility. Therefore, the Ni content is 6 to 55%. In addition, the preferable content of Ni is 10 to 40%, and the more preferable content is more than 15% and 30% or less.

ＲＥＭ：０．２％を超えて０．６％以下
ＲＥＭは、本発明において最も重要な元素の一つである。ＲＥＭはＰとの親和力が大きいため、今まで規制の設けられていた量を超えるＰを含有する場合であっても、溶接凝固中に液相中へ濃化したＰと結びついて燐化物として晶出し、液相の早期消失を促進することで溶接凝固割れ感受性を著しく低減することが可能となる。REM: more than 0.2% and 0.6% or less REM is one of the most important elements in the present invention. Since REM has a large affinity with P, even when it contains P exceeding the amount that has been established so far, it is combined with P concentrated in the liquid phase during weld solidification to form crystals as phosphides. It is possible to significantly reduce the susceptibility to weld solidification cracking by promoting the early disappearance of the liquid phase.

既に述べたＰの含有量範囲内で、上記したＲＥＭの効果を発揮させるためには、０．２％を超える量のＲＥＭを含有させることが必要である。一方、ＲＥＭの含有量が０．６％を超えると、ＲＥＭ燐化物の晶出による液相の早期消失効果が著しく低下し、却って溶接凝固割れ感受性が大きくなり、加えて、ＲＥＭ燐化物の晶出量が増加するために熱間加工性の著しい低下をきたす。   In order to exhibit the above-described REM effect within the P content range already described, it is necessary to contain REM in an amount exceeding 0.2%. On the other hand, if the content of REM exceeds 0.6%, the effect of early disappearance of the liquid phase due to crystallization of REM phosphide is remarkably reduced, and on the contrary, the sensitivity to weld solidification cracking is increased. The increase in the output yields a significant decrease in hot workability.

したがって、ＲＥＭの含有量を０．２％を超えて０．６％以下とした。なお、ＲＥＭの好ましい含有量は０．３％を超えて０．６％以下である。   Therefore, the REM content is set to more than 0.2% and not more than 0.6%. In addition, the preferable content of REM is more than 0.3% and 0.6% or less.

ｓｏｌ．Ａｌ：０．００１〜３％
Ａｌは、オーステナイト系ステンレス鋼の溶製時に脱酸作用を有する。この効果を発揮させるためにはＡｌをｓｏｌ．Ａｌ（「酸可溶性Ａｌ」）として０．００１％以上含有させる必要がある。しかし、ｓｏｌ．ＡｌとしてのＡｌの含有量が３％を超えると、高温での使用中にσ相等の金属間化合物の析出を促進し、靱性や延性、高温強度を低下させる。したがって、ｓｏｌ．Ａｌの含有量は０．００１〜３％とした。なお、ｓｏｌ．Ａｌの含有量は０．００５〜２％であればより好ましく、０．０１〜１％であればさらに好ましい。sol. Al: 0.001 to 3%
Al has a deoxidizing action when austenitic stainless steel is melted. In order to exert this effect, Al is sol. It is necessary to contain 0.001% or more as Al (“acid-soluble Al”). However, sol. When the content of Al as Al exceeds 3%, precipitation of intermetallic compounds such as σ phase is promoted during use at high temperature, and toughness, ductility and high temperature strength are reduced. Therefore, sol. The Al content was 0.001 to 3%. Note that sol. The Al content is more preferably 0.005 to 2%, and further preferably 0.01 to 1%.

Ｎ：０．３％以下
Ｎは、オーステナイトを安定化させる元素であり、クリープ強度を高める作用を有する。しかしながら、Ｎの含有量が過剰になると熱間加工性および冷間加工性の低下をきたし、特に、０．３％を超えると、熱間加工性および冷間加工性の低下が著しくなる。したがって、Ｎの含有量を０．３％以下とした。なお、Ｎの好ましい含有量は０．１％以下であり、さらに好ましい含有量は０．０３％以下である。N: 0.3% or less N is an element that stabilizes austenite and has an effect of increasing creep strength. However, when the N content is excessive, hot workability and cold workability are deteriorated. Particularly, when it exceeds 0.3%, the hot workability and the cold workability are remarkably deteriorated. Therefore, the N content is set to 0.3% or less. In addition, the preferable content of N is 0.1% or less, and the more preferable content is 0.03% or less.

（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）の値：１．３８８未満
上述した範囲のＣからＮまでの元素を含有し、残部がＦｅおよび不純物からなるオーステナイト系ステンレス鋼は、「（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）」の値が１．３８８未満であれば、つまり（１）式を満たせば、完全オーステナイト凝固してオーステナイト単相組織になる場合であっても、溶接凝固割れを確実かつ安定して抑制できる。Value of (Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P): Less than 1.388 The elements from C to N in the above-mentioned range are contained, the balance being Fe and An austenitic stainless steel made of impurities has a value of “(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P)”, that is, (1 If the above formula is satisfied, weld solidification cracks can be reliably and stably suppressed even when complete austenite solidifies to form an austenite single phase structure.

上記の理由から、本発明（１）に係るオーステナイト系ステンレス鋼溶接継手は、母材および溶接金属が、上述した範囲のＣからＮまでの元素を含有し、残部はＦｅおよび不純物からなり、かつ前記（１）式を満たすことと規定した。   For the above reasons, in the austenitic stainless steel welded joint according to the present invention (1), the base metal and the weld metal contain the elements from C to N in the above-mentioned range, and the balance consists of Fe and impurities, and It was defined that the expression (1) was satisfied.

同じ理由で、本発明（３）に係るオーステナイト系ステンレス鋼溶接材料は、上述した範囲のＣからＮまでの元素を含有し、残部はＦｅおよび不純物からなり、かつ前記（１）式を満たすことと規定した。   For the same reason, the austenitic stainless steel welding material according to the present invention (3) contains the elements from C to N in the above-mentioned range, the balance is made of Fe and impurities, and satisfies the formula (1). Stipulated.

なお、本発明（１）に係るオーステナイト系ステンレス鋼溶接継手は、その母材および溶接金属のＦｅの一部に代えて、また、本発明（３）に係るオーステナイト系ステンレス鋼溶接材料は、そのＦｅの一部に代えて、それぞれ、必要に応じてさらに、下記第１群および第２群の中から選ばれた１種または２種以上の元素を含有させることができる。
第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上、
第２群：Ｃａ：０．０５％以下およびＭｇ：０．０５％以下の１種または２種。
The austenitic stainless steel welded joint according to the present invention (1) is replaced with a part of Fe of the base metal and the weld metal, and the austenitic stainless steel welded material according to the present invention (3) is Instead of a part of Fe, one or more elements selected from the following first group and second group can be further contained as necessary.
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: 1.5% or less , B: 0.03% or less, Cu: 3% or less and Co: 5% or less
Second group: one or two of Ca: 0.05% or less and Mg: 0.05% or less.

すなわち、前記第１群および第２群のグループのうちの元素の１種または２種以上を任意元素として含有させてもよい。   That is, one or more elements of the first group and the second group may be included as optional elements.

以下、上記の任意元素に関して説明する。   Hereinafter, the above optional elements will be described.

第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｚｒ：１％以下、Ｈｆ：１％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上
第１群の元素であるＭｏ、Ｗ、Ｔｉ、Ｎｂ、Ｔａ、Ｖ、Ｂ、ＣｕおよびＣｏは、高温強度を高める作用を有するので、この効果を得るために上記の元素を含有させてもよい。以下、第１群の元素について詳しく説明する。
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: One or more elements of 1.5% or less, Zr: 1% or less, Hf: 1% or less, B: 0.03% or less, Cu: 3% or less, and Co: 5% or less Certain Mo, W, Ti, Nb, Ta, V 2 , B, Cu, and Co have the effect of increasing the high-temperature strength. Therefore, the above-described elements may be included to obtain this effect. Hereinafter, the first group of elements will be described in detail.

Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下
ＭｏおよびＷは、高温強度の向上に有効な元素である。Ｍｏには、耐孔食性高める作用もある。上記の効果を確実に得るには、ＭｏとＷをそれぞれ単独で含有させる場合、含有量はそれぞれ０．０５％以上とし、両元素を複合して含有させる場合はＭｏ＋（Ｗ／２）で０．０５％以上とすることが好ましい。しかしながら、単独で含有させる場合、ＭｏおよびＷをそれぞれ、５％および１０％を超えて含有させても、また、複合して含有させる場合、Ｍｏ＋（Ｗ／２）で５％を超えるＭｏとＷを含有させても、前記の効果が飽和してコストが嵩むうえに、ＭｏおよびＷがフェライトを安定化させる元素であるために、σ相等の金属間化合物の生成を誘発し、組織安定性および熱間加工性の劣化を招く。したがって、含有させる場合のＭｏおよびＷの含有量は、Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下とした。ＭｏとＷをそれぞれ単独で含有させる場合の含有量は、Ｍｏは０．０５〜５％、また、Ｗは０．０５〜１０％とすることが好ましく、一方、両元素を複合して含有させる場合の含有量は、Ｍｏ＋（Ｗ／２）で０．０５〜５％とすることが好ましい。Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less Mo and W are effective elements for improving the high-temperature strength. Mo also has an effect of enhancing pitting corrosion resistance. In order to reliably obtain the above effect, when Mo and W are each contained alone, the content is 0.05% or more. When both elements are contained in combination, Mo + (W / 2) is 0. 0.05% or more is preferable. However, when contained alone, Mo and W exceed 5% and 10%, respectively, and when combined, Mo + (W / 2) exceeds 5% Mo and W. In addition, since the effects described above are saturated and the cost is increased, Mo and W are elements that stabilize ferrite, so the formation of intermetallic compounds such as σ phase is induced, and the structure stability and It causes deterioration of hot workability. Therefore, the contents of Mo and W in the case of inclusion were set to Mo: 5% or less, W: 10% or less, and Mo + (W / 2): 5% or less. When Mo and W are contained individually, the content of Mo is preferably 0.05 to 5%, and W is preferably 0.05 to 10%. On the other hand, both elements are combined and contained. In this case, the content of Mo + (W / 2) is preferably 0.05 to 5%.

なお、上述のとおり、ＭｏおよびＷはフェライト形成元素であるため、オーステナイト組織の安定化のためには、ＭｏとＷをそれぞれ単独で含有させる場合の含有量は、Ｍｏは０．０５％以上４％未満、また、Ｗは０．０５％以上４％未満とすることがより好ましい。   As described above, since Mo and W are ferrite forming elements, in order to stabilize the austenite structure, the content when Mo and W are contained alone is 0.05% or more and 4%, respectively. % And W is more preferably 0.05% or more and less than 4%.

Ｔｉ：３％以下
Ｔｉは、炭化物形成元素であり、高温強度の向上に有効な元素である。Ｔｉには、Ｃを固定して粒界耐食性を高める作用もある。これらの効果を確実に得るには、Ｔｉの含有量は０．００５％以上とすることが望ましい。しかしながら、Ｔｉの含有量が３％を超えると、靱性を始めとする機械的性質の大きな劣化を招く。したがって、含有させる場合のＴｉの含有量は、３％以下とした。なお、含有させる場合のＴｉの含有量は、０．００５〜３％とすることが好ましく、０．０１〜２％であればより好ましい。含有させる場合のＴｉの含有量は、０．０５〜１％であれば極めて好ましい。Ti: 3% or less Ti is a carbide forming element and is an element effective for improving high-temperature strength. Ti also has the effect of fixing C and increasing the grain boundary corrosion resistance. In order to reliably obtain these effects, the Ti content is desirably 0.005% or more. However, when the Ti content exceeds 3%, mechanical properties such as toughness are greatly deteriorated. Therefore, when Ti is contained, the content of Ti is set to 3% or less. In addition, when Ti is contained, the content of Ti is preferably 0.005 to 3%, and more preferably 0.01 to 2%. When Ti is contained, the content of Ti is extremely preferably 0.05 to 1%.

Ｎｂ：１．５％以下
Ｎｂは、炭化物形成元素であり、高温強度の向上に有効な元素である。Ｎｂには、Ｃを固定して粒界耐食性を高める作用もある。こうした効果を確実に得るには、Ｎｂの含有量は０．０５％以上とすることが望ましい。しかしながら、Ｎｂの含有量が１．５％を超えると、靱性を始めとする機械的性質の大きな劣化を招く。したがって、含有させる場合のＮｂの含有量は、１．５％以下とした。なお、含有させる場合のＮｂの含有量は、０．０５〜１．５％とすることが好ましく、０．０５〜１％であればより好ましい。含有させる場合のＮｂの含有量は、０．０５〜０．６％であれば極めて好ましい。Nb: 1.5% or less Nb is a carbide forming element and is an element effective for improving high-temperature strength. Nb also has the effect of fixing C and increasing the grain boundary corrosion resistance. In order to reliably obtain such an effect, the Nb content is desirably 0.05% or more. However, when the Nb content exceeds 1.5%, mechanical properties such as toughness are greatly deteriorated. Therefore, when Nb is included, the content of Nb is set to 1.5% or less. In addition, when Nb is contained, the content of Nb is preferably 0.05 to 1.5%, and more preferably 0.05 to 1%. When Nb is contained, the content of Nb is extremely preferably 0.05 to 0.6%.

Ｔａ：８％以下
Ｔａも炭化物形成元素であり、高温強度の向上に有効である。Ｔａには、Ｃを固定して粒界耐食性を高める作用もある。これらの効果を確実に得るには、Ｔａの含有量は０．０１％以上とすることが望ましい。しかしながら、Ｔａの含有量が８％を超えると、靱性を始めとする機械的性質の大きな劣化を招く。したがって、含有させる場合のＴａの含有量は、８％以下とした。なお、含有させる場合のＴａの含有量は、０．０１〜８％とすることが好ましく、０．０１〜７％であればより好ましい。含有させる場合のＴａの含有量は、０．０５〜６％であれば極めて好ましい。Ta: 8% or less Ta is also a carbide forming element and is effective in improving high temperature strength. Ta also has the effect of fixing C and increasing the grain boundary corrosion resistance. In order to reliably obtain these effects, the Ta content is desirably 0.01% or more. However, when the Ta content exceeds 8%, mechanical properties such as toughness are greatly deteriorated. Therefore, when Ta is included, the content of Ta is set to 8% or less. In addition, when Ta is included, the content of Ta is preferably 0.01 to 8%, and more preferably 0.01 to 7%. When Ta is included, the content of Ta is very preferably 0.05 to 6%.

Ｖ：１．５％以下
Ｖは、炭化物形成元素であり、高温強度の向上に有効である。Ｖにも、Ｃを固定して粒界耐食性を高める作用もある。こうした効果を確実に得るには、Ｖの含有量は０．０２％以上とすることが望ましい。しかしながら、Ｖの含有量が１．５％を超えると、靱性を始めとする機械的性質の大きな劣化を招く。したがって、含有させる場合のＶの含有量は、１．５％以下とした。なお、含有させる場合のＶの含有量は、０．０２〜１．５％とすることが好ましく、０．０４〜１％であればより好ましい。V: 1.5% or less V is a carbide forming element and is effective in improving high-temperature strength. V also has the effect of fixing C and increasing the grain boundary corrosion resistance. In order to obtain such an effect reliably, the V content is preferably 0.02% or more. However, if the V content exceeds 1.5%, mechanical properties such as toughness are greatly deteriorated. Therefore, when V is included, the content of V is set to 1.5% or less. In addition, when V is included, the content of V is preferably 0.02 to 1.5%, and more preferably 0.04 to 1%.

Ｂ：０．０３％以下
Ｂは、炭窒化物中に存在して高温での使用中における炭窒化物の微細分散析出を促進するとともに、Ｂ単体で粒界に存在して粒界を強化し粒界すべりを抑制することによって、高温強度を高めるとともにクリープ強度を改善する。こうした効果を確実に得るには、Ｂの含有量は０．０００５％以上とすることが望ましい。しかしながら、Ｂの含有量が０．０３％を超えると、溶接性の劣化をきたす。したがって、含有させる場合のＢの含有量は、０．０３％以下とした。なお、含有させる場合のＢの含有量は、０．０００５〜０．０３％とすることが好ましく、０．００１〜０．０１％であればより好ましい。含有させる場合のＢの含有量は、０．００１〜０．００５％であれば極めて好ましい。B: 0.03% or less B is present in carbonitride and promotes fine dispersion precipitation of carbonitride during use at high temperature, and B alone exists at the grain boundary to strengthen the grain boundary. By suppressing grain boundary sliding, the high temperature strength is increased and the creep strength is improved. In order to reliably obtain such an effect, the B content is desirably 0.0005% or more. However, when the content of B exceeds 0.03%, weldability is deteriorated. Therefore, when B is included, the content of B is set to 0.03% or less. When B is included, the content of B is preferably 0.0005 to 0.03%, more preferably 0.001 to 0.01%. When B is contained, the content of B is very preferably 0.001 to 0.005%.

Ｃｕ：３％以下
Ｃｕは、オーステナイトを安定化し、かつ高温での使用中に微細なＣｕ相としてオーステナイト母相に整合析出し、高温強度を大幅に向上させる作用を有する。上記の効果を確実に得るには、Ｃｕの含有量は０．０１％以上とすることが望ましい。しかしながら、Ｃｕの含有量が多くなり、特に３％を超えると、熱間加工性、溶接性およびクリープ延性の低下を招く。したがって、例えば、原料コストの面からＮｉに代わってオーステナイトを安定化させたり一層大きな高温強度を確保することを目的として含有させる場合のＣｕの含有量は、３％以下とした。なお、含有させる場合のＣｕの含有量は、０．０１〜３％とすることが好ましい。含有させる場合のＣｕ含有量の上限は、２％であればより好ましく、０．９％であれば極めて好ましい。Cu: 3% or less Cu stabilizes austenite and co-precipitates in the austenite matrix as a fine Cu phase during use at high temperature, and has the effect of greatly improving high-temperature strength. In order to surely obtain the above effect, the Cu content is desirably 0.01% or more. However, if the Cu content increases, especially exceeding 3%, the hot workability, weldability and creep ductility are reduced. Therefore, for example, the Cu content is set to 3% or less in the case of containing austenite for the purpose of stabilizing austenite or securing a higher high-temperature strength in place of Ni in terms of raw material cost. In addition, it is preferable that content of Cu when making it contain is 0.01 to 3%. The upper limit of the Cu content in the case of inclusion is more preferably 2%, and extremely preferably 0.9%.

Ｃｏ：５％以下
Ｃｏは、ＮｉやＣｕと同様にオーステナイト組織を安定化し、高温強度を高める作用を有する。この効果を確実に得るには、Ｃｏの含有量は０．０５％以上とすることが望ましい。しかしながら、Ｃｏの含有量が５％を超えても前記の効果は飽和し、経済性が低下するばかりである。したがって、含有させる場合のＣｏの含有量は、５％以下とした。なお、含有させる場合のＣｏの含有量は、０．０５〜５％とすることが好ましい。Co: 5% or less Co, like Ni and Cu, has the effect of stabilizing the austenite structure and increasing the high temperature strength. In order to reliably obtain this effect, the Co content is desirably 0.05% or more. However, even if the Co content exceeds 5%, the above-mentioned effect is saturated and the economic efficiency is lowered. Therefore, the Co content when contained is set to 5% or less. In addition, when Co is contained, the content of Co is preferably 0.05 to 5%.

なお、上記のＭｏ、Ｗ、Ｔｉ、Ｎｂ、Ｔａ、Ｖ、Ｂ、ＣｕおよびＣｏは、そのうちのいずれか１種のみ、または２種以上の複合で含有させることができる。
In addition, said Mo, W, Ti, Nb, Ta, V , B, Cu, and Co can be contained only in any 1 type or 2 or more types of composites.

第２群の元素であるＣａおよびＭｇは熱間加工性を高める作用を有するので、この効果を得るために上記の元素を含有させてもよい。以下、第２群の元素について詳しく説明する。   Since the elements of the second group, Ca and Mg, have the effect of improving the hot workability, the above elements may be included to obtain this effect. Hereinafter, the second group of elements will be described in detail.

Ｃａ：０．０５％以下
Ｃａは、熱間加工性を高める作用を有する。この効果を確実に得るには、Ｃａの含有量は０．０００５％以上とすることが好ましい。しかしながら、Ｃａの含有量が０．０５％を超えると、酸化物系介在物を形成し却って熱間加工性が低下し、延性の劣化も生じる。したがって、含有させる場合のＣａの含有量は、０．０５％以下とした。なお、含有させる場合のＣａの含有量は、０．０００５〜０．０５％とすることが好ましく、０．００１〜０．０２％であればより好ましい。含有させる場合のＣａの含有量は、０．００１〜０．０１％であれば極めて好ましい。Ca: 0.05% or less Ca has an effect of improving hot workability. In order to reliably obtain this effect, the Ca content is preferably 0.0005% or more. However, if the Ca content exceeds 0.05%, oxide inclusions are formed and hot workability is lowered, and ductility is also deteriorated. Therefore, when Ca is contained, the content of Ca is set to 0.05% or less. In addition, when Ca is contained, the content of Ca is preferably 0.0005 to 0.05%, and more preferably 0.001 to 0.02%. When Ca is contained, the content of Ca is extremely preferably 0.001 to 0.01%.

Ｍｇ：０．０５％以下
Ｍｇも熱間加工性を高める作用を有する。この効果を確実に得るには、Ｍｇの含有量は０．０００５％以上とすることが好ましい。しかしながら、Ｍｇの含有量が０．０５％を超えると、酸化物系介在物を形成し却って熱間加工性が低下し、延性の劣化も生じる。したがって、含有させる場合のＭｇの含有量は、０．０５％以下とした。なお、含有させる場合のＭｇの含有量は、０．０００５〜０．０５％とすることが好ましく、０．００１〜０．０２％であればより好ましい。含有させる場合のＭｇの含有量は、０．００１〜０．０１％であれば極めて好ましい。Mg: 0.05% or less Mg also has an effect of improving hot workability. In order to reliably obtain this effect, the Mg content is preferably 0.0005% or more. However, if the Mg content exceeds 0.05%, oxide-based inclusions are formed and hot workability is lowered, and ductility is also deteriorated. Therefore, when Mg is contained, the content of Mg is set to 0.05% or less. When Mg is included, the content of Mg is preferably 0.0005 to 0.05%, and more preferably 0.001 to 0.02%. When Mg is contained, the content of Mg is extremely preferably 0.001 to 0.01%.

なお、上記のＣａおよびＭｇは、そのうちのいずれか１種のみ、または２種の複合で含有させることができる。   In addition, said Ca and Mg can be contained only in any 1 type in them, or 2 types of composites.

（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）の値：１．３８８未満
前記本発明（１）に係るオーステナイト系ステンレス鋼溶接継手の母材および溶接金属のＦｅの一部に代えて、また、本発明（３）に係るオーステナイト系ステンレス鋼溶接材料のＦｅの一部に代えて、上記第１群および第２群の中から選ばれた１種または２種以上の元素を含有するオーステナイト系ステンレス鋼は、「（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）」の値が１．３８８未満であれば、つまり（２）式を満たせば、完全オーステナイト凝固してオーステナイト単相組織になる場合であっても、溶接凝固割れを確実かつ安定して抑制できる。(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P): less than 1.388 Mother of the austenitic stainless steel welded joint according to the present invention (1) Selected from the first group and the second group in place of a part of Fe of the metal and the weld metal and in place of a part of Fe of the austenitic stainless steel welding material according to the present invention (3). In addition, the austenitic stainless steel containing one or more elements has a value of “(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P)”. If it is less than 1.388, that is, if equation (2) is satisfied, weld solidification cracking is ensured even in the case of complete austenite solidification and austenite single phase structure. One can be stably suppressed.

上記の理由から、本発明（２）に係るオーステナイト系ステンレス鋼溶接継手および本発明（４）に係るオーステナイト系ステンレス鋼溶接材料は、本発明（１）に係るオーステナイト系ステンレス鋼溶接継手および本発明（３）に係るオーステナイト系ステンレス鋼溶接材料のＦｅの一部に代えて、上記第１群および第２群の中から選ばれた１種または２種以上の元素を含有し、かつ前記（２）式を満たすことと規定した。   For the above reasons, the austenitic stainless steel welded joint according to the present invention (2) and the austenitic stainless steel welded material according to the present invention (4) are the austenitic stainless steel welded joint according to the present invention (1) and the present invention. Instead of a part of Fe of the austenitic stainless steel welding material according to (3), it contains one or more elements selected from the first group and the second group, and (2 ) Formula is satisfied.

本発明（１）および本発明（２）に係るオーステナイト系ステンレス鋼溶接継手は、ＴＩＧ溶接、ＭＩＧ溶接等の種々の溶接方法で作製することができる。   The austenitic stainless steel welded joint according to the present invention (1) and the present invention (2) can be produced by various welding methods such as TIG welding and MIG welding.

なお、上記のオーステナイト系ステンレス鋼溶接継手の作製に用いる溶接材料としては、採用する溶接方法と溶接条件に応じて、前記の溶接金属の組成が得られる組成のものを選べばよい。   In addition, what is necessary is just to select the thing of the composition from which the composition of the said weld metal is obtained as a welding material used for preparation of said austenitic stainless steel welded joint according to the welding method and welding conditions to employ | adopt.

ＴＩＧ溶接を採用する場合には、溶接材料の組成は実質的に溶接金属の組成と同じでよいので、例えば、本発明（１）に係るオーステナイト系ステンレス鋼溶接継手の作製に用いる溶接材料としては本発明（３）に係るオーステナイト系ステンレス鋼溶接材料を用いるのが望ましく、また、本発明（２）に係るオーステナイト系ステンレス鋼溶接継手の作製に用いる溶接材料としては本発明（４）に係るオーステナイト系ステンレス鋼溶接材料を用いるのが望ましい。   When TIG welding is adopted, the composition of the welding material may be substantially the same as the composition of the weld metal. For example, as the welding material used for the production of the austenitic stainless steel welded joint according to the present invention (1), It is desirable to use the austenitic stainless steel welding material according to the present invention (3), and as the welding material used for producing the austenitic stainless steel welded joint according to the present invention (2), the austenite according to the present invention (4) is used. It is desirable to use a stainless steel welding material.

以下、実施例によって本発明をより具体的に説明するが、本発明はこれらの実施例に限定されるものではない。   EXAMPLES Hereinafter, although an Example demonstrates this invention more concretely, this invention is not limited to these Examples.

表１に示す化学組成を有するオーステナイト系ステンレス鋼である鋼１〜９および鋼Ａ〜Ｅを高周波加熱真空炉を用いて溶解した後、インゴットに鋳造した。   Steels 1 to 9 and steels A to E, which are austenitic stainless steels having the chemical composition shown in Table 1, were melted using a high-frequency heating vacuum furnace, and then cast into ingots.

表１中の鋼１〜９は、化学組成が本発明で規定する範囲内にある鋼である。一方、表１中の鋼Ａ〜Ｅは、化学組成が本発明で規定する条件から外れた比較例の鋼である。   Steels 1 to 9 in Table 1 are steels whose chemical compositions are within the range defined by the present invention. On the other hand, steels A to E in Table 1 are steels of comparative examples whose chemical compositions deviate from the conditions defined in the present invention.

Figure 0005218065
Figure 0005218065

得られた各インゴットを通常の方法で熱間鍛造した後、１２００℃で固溶化熱処理を施し、突き合わせ部１．５ｍｍの６０°Ｖ開先加工が施された厚さ１２ｍｍ、幅５０ｍｍおよび長さ１５０ｍｍの拘束溶接割れ試験用試験片、ならびに、厚さ４ｍｍ、幅１００ｍｍおよび長さ１００ｍｍのトランスバレストレイン試験片を作製した。   Each of the obtained ingots was hot forged by a normal method, then subjected to a solution heat treatment at 1200 ° C., and a butt portion of 1.5 mm was subjected to 60 ° V groove processing, a thickness of 12 mm, a width of 50 mm, and a length. A 150 mm-constraint weld cracking test piece and a transvalestrain test piece having a thickness of 4 mm, a width of 100 mm, and a length of 100 mm were prepared.

なお、鋼Ｃおよび鋼Ｄは、本発明で規定する値を超える過剰なＮｄを含むため熱間加工性が低く、熱間鍛造時に多数の割れを生じて試験片が採取できなかった。これは、Ｎｄの含有量が過剰のために多量のＮｄＰが早期に晶出しすぎてしまい、液相の早期消失効果を得られず、逆に凝固割れ感受性が増大したため、またはＮｄＰが晶出せずにＮｄ単独の偏析も重畳したことによって、固液共存温度範囲が著しく増大してしまい凝固割れ感受性が増大したためと考えられる。そして、上記の熱間鍛造時に発生した割れは、低融点粒界の融解、すなわち、Ｐの著しい粒界偏析に起因した凝固割れであり、溶接試験に供するまでもなく凝固割れ感受性が著しく高いと考えられ、実用鋼として適用することは困難である。   Steel C and steel D contain excessive Nd exceeding the value specified in the present invention, so the hot workability is low, and a large number of cracks were generated during hot forging, and specimens could not be collected. This is because a large amount of NdP is crystallized too early due to excessive Nd content, so that the effect of early disappearance of the liquid phase cannot be obtained, and conversely, the susceptibility to solidification cracking has increased, or NdP does not crystallize. This is also because the solid-liquid coexistence temperature range was remarkably increased due to the superposition of segregation of Nd alone, and the solidification cracking sensitivity was increased. And the crack which generate | occur | produced at the time of said hot forging is a solidification crack resulting from melting of a low melting-point grain boundary, ie, the remarkable grain boundary segregation of P, and it does not use for a welding test, It is considered that it is difficult to apply as practical steel.

上記のようにして得た各オーステナイト系ステンレス鋼の拘束溶接割れ試験用試験片を用いて、周囲を拘束溶接した。また、あらかじめ各オーステナイト系ステンレス鋼の母材から作製した外径１．２ｍｍの溶接材料（溶接ワイヤー）を使用して、溶接電流１６５Ａ、溶接電圧１５Ｖ、溶接速度１０ｃｍ／ｍｉｎの条件にてＴＩＧ溶接により突き合わせ部分に対してフィラー溶接を行った。   Using the test pieces for restraint welding crack test of each austenitic stainless steel obtained as described above, the surroundings were restrained and welded. In addition, TIG welding is performed using a welding material (welding wire) with an outer diameter of 1.2 mm prepared in advance from a base material of each austenitic stainless steel under the conditions of a welding current of 165 A, a welding voltage of 15 V, and a welding speed of 10 cm / min. Thus, filler welding was performed on the butt portion.

表２に、拘束溶接割れ試験片の溶接ビード長に対する凝固割れ発生率の測定結果を示す。ここで、溶接金属の化学組成は、ＴＩＧ溶接の場合希釈はほとんど生じないため、母材と同一である。   Table 2 shows the measurement results of the solidification crack occurrence rate with respect to the weld bead length of the restrained weld crack test piece. Here, the chemical composition of the weld metal is the same as that of the base material because dilution hardly occurs in TIG welding.

なお、上述のとおり、鋼Ｃおよび鋼Ｄは、熱間鍛造時に割れを生じて試験片が採取できなかった。このため、拘束溶接割れ試験を実施できなかったので、表２の「拘束溶接割れ試験でのビード表面割れ率」欄は「−」と表記した。   As described above, Steel C and Steel D were cracked during hot forging, and specimens could not be collected. For this reason, since the restraint weld cracking test could not be performed, the “bead surface crack ratio in the restraint weld cracking test” column of Table 2 was indicated as “−”.

Figure 0005218065
Figure 0005218065

また、各オーステナイト系ステンレス鋼の凝固割れ感受性をより詳細に評価するために、前記のトランスバレストレイン試験片を用いて、溶接電流１００Ａ、溶接電圧１５Ｖ、溶接速度１５ｃｍ／ｍｉｎ、付加歪み２％の条件にてトランスバレストレイン試験を行い、最大割れ長さを測定した。   Moreover, in order to evaluate the solidification cracking susceptibility of each austenitic stainless steel in more detail, a welding current of 100 A, a welding voltage of 15 V, a welding speed of 15 cm / min, and an additional strain of 2% were used. The transbalance test was performed under the conditions, and the maximum crack length was measured.

なお、完全オーステナイト凝固するオーステナイト系ステンレス鋼であるＳＵＳ３１０Ｓの溶接金属のトランスバレストレイン試験により評価された最大割れ長さは１ｍｍ以下である。したがって、トランスバレストレイン試験により評価された最大割れ長さが１ｍｍ以下のオーステナイト系ステンレス鋼は優れた耐凝固割れ性を有していると考えられる。   It should be noted that the maximum crack length evaluated by the transbarestrain test of the weld metal of SUS310S, which is an austenitic stainless steel that completely solidifies austenite, is 1 mm or less. Therefore, it is considered that the austenitic stainless steel having a maximum crack length of 1 mm or less evaluated by the transbalance train test has excellent solidification cracking resistance.

表２に、トランスバレストレイン試験での最大割れ長さを併せて示す。   Table 2 also shows the maximum crack length in the transbalance train test.

なお、上述のとおり、鋼Ｃおよび鋼Ｄは、熱間鍛造時に割れを生じて試験片が採取できなかったため、トランスバレストレイン試験を実施できなかった。このため、表２の「トランスバレストレイン試験での最大割れ長さ」欄は「−」と表記した。   In addition, as above-mentioned, since the steel C and the steel D produced the crack at the time of hot forging and the test piece was not able to be extract | collected, the transbalance test could not be implemented. For this reason, the “maximum crack length in the transbalance train test” column of Table 2 is indicated as “−”.

表２から、本発明で規定する条件を満たす鋼１〜９の場合、高い量のＰを含み、しかも、完全オーステナイト凝固するにも拘わらず、適正量のＲＥＭを含むとともに式（１）または式（２）を満足しているので、トランスバレストレイン試験による最大割れ長さが全て１ｍｍ以下であり、かつ拘束溶接割れ試験においても割れが発生しておらず、良好な溶接性を有していることが明らかである。   From Table 2, in the case of steels 1 to 9 that satisfy the conditions specified in the present invention, a high amount of P is included, and despite the complete austenite solidification, an appropriate amount of REM is included and the formula (1) or Since (2) is satisfied, all the maximum crack lengths by the trans-balest train test are 1 mm or less, and no cracks are generated in the restrained weld crack test, and the weldability is good. It is clear.

これに対して、本発明で規定する条件から外れた比較例の鋼Ａ、鋼Ｂおよび鋼Ｅは、溶接性が劣っている。   On the other hand, the steel A, steel B, and steel E of comparative examples that deviate from the conditions defined in the present invention have poor weldability.

すなわち、鋼Ａの場合、Ｎｄの含有量が０．１３％と低いため、ＮｄＰの晶出を促進できない。したがって、拘束溶接割れ試験におけるビード表面割れ率は０％であるものの、トランスバレストレイン最大割れ長さは１ｍｍを超えている。   That is, in the case of Steel A, the Nd content is as low as 0.13%, so that crystallization of NdP cannot be promoted. Therefore, although the bead surface crack rate in the constrained weld cracking test is 0%, the maximum transvaletrain crack length exceeds 1 mm.

鋼Ｂの場合、Ｎｄの含有量が０．０３５％と低く、しかも、式（２）の条件を満たさない。このため、ＮｄＰの晶出を促進できないので、完全オーステナイト凝固でないにも拘わらず、トランスバレストレイン最大割れ長さは１ｍｍを超えており、また、拘束溶接割れ試験におけるビード表面割れ率は１００％であり、ビード全長に渡って割れが発生している。   In the case of steel B, the Nd content is as low as 0.035%, and the condition of formula (2) is not satisfied. For this reason, since crystallization of NdP cannot be promoted, the maximum crack length of transbaretrain exceeds 1 mm in spite of not complete austenite solidification, and the bead surface crack rate in the constrained weld crack test is 100%. Yes, cracks occur along the entire length of the bead.

鋼Ｅの場合、式（２）の条件を満たしているが、Ｐの含有量が高いにも拘わらずＮｄを含んでいない。このため、溶接凝固割れ感受性は著しく高く、トランスバレストレイン最大割れ長さは１ｍｍを超えており、また、拘束溶接割れ試験におけるビード表面割れ率は１００％であり、ビード全長に渡って割れが発生している。   In the case of steel E, the condition of the formula (2) is satisfied, but Nd is not included even though the content of P is high. For this reason, the weld solidification cracking susceptibility is extremely high, the maximum crack length of the trans-bare train exceeds 1 mm, and the bead surface cracking rate in the restrained weld cracking test is 100%, and cracking occurs over the entire bead length. doing.

なお、既に述べたように、鋼Ｃおよび鋼Ｄは、本発明で規定する値を超える過剰なＮｄを含むため熱間加工性が低い。これは、Ｎｄの含有量が過剰のために多量のＮｄＰが早期に晶出しすぎてしまい、液相の早期消失効果を得られず、逆に凝固割れ感受性が増大したため、またはＮｄＰが晶出せずにＮｄ単独の偏析も重畳したことによって、固液共存温度範囲が著しく増大してしまい凝固割れ感受性が増大したためと考えられ、実用鋼として適用することは困難である。   As already described, steel C and steel D have excessive hot workability because they contain excess Nd exceeding the value specified in the present invention. This is because a large amount of NdP is crystallized too early due to excessive Nd content, so that the effect of early disappearance of the liquid phase cannot be obtained, and conversely, the susceptibility to solidification cracking has increased, or NdP does not crystallize. Further, it is considered that the segregation of Nd alone is also superimposed, so that the solid-liquid coexistence temperature range is remarkably increased and the solidification cracking sensitivity is increased, and it is difficult to apply as practical steel.

本発明の母材および溶接金属から成るオーステナイト系ステンレス鋼溶接継手は、Ｐ含有量が高く、しかも、完全オーステナイト凝固するにも拘わらず、優れた耐溶接凝固割れ性を有しているので、溶接施工が要求される用途に幅広く適用することができる。また、本発明のオーステナイト系ステンレス鋼溶接材料は、上記のオーステナイト系ステンレス鋼溶接継手を作製するのに最適である。   The austenitic stainless steel welded joint composed of the base material and the weld metal of the present invention has a high P content and has excellent weld solidification cracking resistance despite complete solidification of austenite. It can be widely applied to applications that require construction. Moreover, the austenitic stainless steel welding material of the present invention is optimal for producing the austenitic stainless steel welded joint.

Claims (4)

母材および溶接金属が、質量％で、Ｃ：０．３％以下、Ｓｉ：１％以下、Ｍｎ：０．０１〜３．０％、Ｐ：０．０４％を超えて０．３％以下、Ｓ：０．０１％以下、Ｃｒ：１２〜３０％、Ｎｉ：１０〜４０％、希土類元素：０．２％を超えて０．６％以下、ｓｏｌ．Ａｌ：０．００１〜３％およびＮ：０．３％以下を含有し、残部がＦｅおよび不純物からなり、かつ下記（１）式を満足することを特徴とするオーステナイト系ステンレス鋼溶接継手。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）＜１．３８８・・・（１）
ここで（１）式中の元素記号は、その元素の質量％での含有量を表す。 Base material and weld metal in mass%, C: 0.3% or less, Si: 1% or less, Mn: 0.01 to 3.0%, P: more than 0.04% and 0.3% or less , S: 0.01% or less, Cr: 12-30%, Ni: 10-40% , rare earth element: more than 0.2% and 0.6% or less, sol. An austenitic stainless steel welded joint containing Al: 0.001 to 3% and N: 0.3% or less, the balance being Fe and impurities, and satisfying the following formula (1).
(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P) <1.388 (1)
Here, the element symbol in the formula (1) represents the content in mass% of the element. Ｆｅの一部に代えて、質量％で、さらに、下記第１群および第２群の中から選ばれた１種または２種以上の元素を含有し、かつ下記（２）式を満足することを特徴とする請求項１に記載のオーステナイト系ステンレス鋼溶接継手。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）＜１．３８８・・・（２）
ここで（２）式中の元素記号は、その元素の質量％での含有量を表す。
第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上
第２群：Ｃａ：０．０５％以下およびＭｇ：０．０５％以下の１種または２種 In place of a part of Fe, in mass%, and further containing one or more elements selected from the following first group and second group, and satisfying the following formula (2) The austenitic stainless steel welded joint according to claim 1.
(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P) <1.388 (2)
Here, the element symbol in the formula (2) represents the content in mass% of the element.
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: One or more of 1.5% or less , B: 0.03% or less, Cu: 3% or less, and Co: 5% or less Second group: Ca: 0.05% or less and Mg: 0.05% One or two of the following 質量％で、Ｃ：０．３％以下、Ｓｉ：１％以下、Ｍｎ：０．０１〜３．０％、Ｐ：０．０４％を超えて０．３％以下、Ｓ：０．０１％以下、Ｃｒ：１２〜３０％、Ｎｉ：１０〜４０％、希土類元素：０．２％超えて０．６％以下、ｓｏｌ．Ａｌ：０．００１〜３％およびＮ：０．３％以下を含有し、残部がＦｅおよび不純物からなり、かつ下記（１）式を満足することを特徴とするオーステナイト系ステンレス鋼溶接材料。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋５×Ｐ）＜１．３８８・・・（１）
ここで（１）式中の元素記号は、その元素の質量％での含有量を表す。 In mass%, C: 0.3% or less, Si: 1% or less, Mn: 0.01 to 3.0%, P: more than 0.04% and 0.3% or less, S: 0.01% Hereinafter, Cr: 12 to 30%, Ni: 10 to 40% , rare earth element: more than 0.2% to 0.6% or less, sol. An austenitic stainless steel welding material characterized by containing Al: 0.001 to 3% and N: 0.3% or less, the balance being Fe and impurities, and satisfying the following formula (1).
(Cr + 1.5 × Si + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + 5 × P) <1.388 (1)
Here, the element symbol in the formula (1) represents the content in mass% of the element. Ｆｅの一部に代えて、質量％で、さらに、下記第１群および第２群の中から選ばれた１種または２種以上の元素を含有し、かつ下記（２）式を満足することを特徴とする請求項３に記載のオーステナイト系ステンレス鋼溶接材料。
（Ｃｒ＋１．５×Ｓｉ＋２×Ｎｂ＋Ｔｉ＋２×Ｐ）／（Ｎｉ＋０．３１×Ｍｎ＋２２×Ｃ＋１４．２×Ｎ＋Ｃｕ＋５×Ｐ）＜１．３８８・・・（２）
ここで（２）式中の元素記号は、その元素の質量％での含有量を表す。
第１群：Ｍｏ：５％以下、Ｗ：１０％以下でかつＭｏ＋（Ｗ／２）：５％以下、Ｔｉ：３％以下、Ｎｂ：１．５％以下、Ｔａ：８％以下、Ｖ：１．５％以下、Ｂ：０．０３％以下、Ｃｕ：３％以下およびＣｏ：５％以下の１種または２種以上
第２群：Ｃａ：０．０５％以下およびＭｇ：０．０５％以下の１種または２種
In place of a part of Fe, in mass%, and further containing one or more elements selected from the following first group and second group, and satisfying the following formula (2) The austenitic stainless steel welding material according to claim 3.
(Cr + 1.5 × Si + 2 × Nb + Ti + 2 × P) / (Ni + 0.31 × Mn + 22 × C + 14.2 × N + Cu + 5 × P) <1.388 (2)
Here, the element symbol in the formula (2) represents the content in mass% of the element.
First group: Mo: 5% or less, W: 10% or less and Mo + (W / 2): 5% or less, Ti: 3% or less, Nb: 1.5% or less, Ta: 8% or less, V: One or more of 1.5% or less , B: 0.03% or less, Cu: 3% or less, and Co: 5% or less Second group: Ca: 0.05% or less and Mg: 0.05% One or two of the following
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